Porous carbons

ABSTRACT

Porous carbon is provided which is a carbonization and optionally an activation product of a precursor resin, which has a pore structure that, as estimated by nitrogen adsorption porosimetry, comprises micropores and mesopores/macropores, said micropores and mesopores/macropores being in a bimodal distribution with few pores of size 2-10 nm, and the mesopores/macropores providing escape routes for volatile products during carbonisation of the precursor resin. 
     The porous carbon can be made by a method which comprises (a) forming a precursor resin by reacting a nucleophilic component which comprises a phenolic compound or a phenol condensation prepolymer optionally with one or more modifying reagents with an electrophilic cross-linking agent selected from formaldehyde, paraformaldehyde, furfural and hexamethylene tetramine in solution in a pore former e.g. ethylene glycol so that a phase separation occurs between high molecular weight domains and voids of lower molecular weight material and the pore former increases the material in the voids and gives rise to the mesopores in the precursor resin; (b) removing the pore former from the precursor resin; and (c) carbonizing the precursor resin in an inert atmosphere at a temperature from 600° C. upwards, micropores developing during said carbonization so that the carbonized material comprises (a) micropores of diameter of up to 2 nm and (b) mesopores of diameter of 2-50 nm and optionally macropores of diameter &gt;50 nm.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation in part of U.S. patent application Ser. No. 11/786,074 filed 10 Apr. 2007 which was a divisional application of U.S. patent application Ser. No. 10/344,248 filed 29 May 2003, now abandoned, which was derived from International Application No. PCT/GB01/03560 filed 7 Aug. 2001 which claimed priority from UK Patent Application No. 00/19417 filed 9 Aug. 2000. The disclosures of these earlier applications are incorporated herein in their entirety.

FIELD OF THE INVENTION

The present invention relates to porous carbons and to methods for making them.

BACKGROUND TO THE INVENTION

Mesoporous carbons are used as adsorbents or catalysts supports and can be used in spherical, granular of thin film form. Existing production methods use gas phase and chemical activation routes to produce mesoporous carbons but, Activated carbon, as conventionally produced, is normally microporous (<2 nm pore diameter—IUPAC definition) with little or no pore volume in the mesopore (2-50 nm) and macropore (>50 nm) range. For some critical adsorption processes such as evaporative emission control, and when used as a catalyst support, particularly in liquid phase applications, this is a major drawback.

Conventional activated carbons can be made mesoporous through severe activation but this seriously degrades their mechanical properties and the materials are generally then only available as fine powders. U.S. Pat. No. 4,677,086 discloses the use of chemical activation to produce mesoporous carbons without such severe mechanical degradation and which also can be produced as extrudates. These are however still produced as powders and must then be bound to produce, for instance, extrudate for use in fixed bed gas phase processes. In most cases the binders that can be used are polymeric or ceramic which then restricts the conditions under which the carbons can be used.

Chemical activation can also be used to directly produce mesoporous carbons by pelleting or extruding a plasticised acidic lignin base char and then directly carbonising and activating the mixture as disclosed in U.S. Pat. No. 5,324,703. The production route also leads to a low macroporosity, which can have disadvantages in catalytic and liquid phase processes. The route also has the disadvantage of requiring compounds such as phosphoric acid and zinc chloride as the activating agents, which can cause severe environmental problems and have a major impact on the materials of construction of the process plant.

Phenolic resins can be carbonised to form mesoporous carbons.

As to the technical background concerning phenolic resins, sulphonated phenolic resins were first used as ion exchange resins in the 1930's (Adams et al, J Soc Chem Ind., 54, (1935) 1-GT) and relatively stable cation and anion exchange resins were used extensively for the softening and demineralisation of water. Other phenolic based resins include the weak base anion exchange resins that have been primarily used in food processing applications (Cristal M J, Chem and Ind, 814, (1983) Nov. 7) and chelation resins which can be produced to give remarkable selectivity for the adsorption of metal ions such as cesium (U.S. Pat. No. 4,423,159, 1983 and U.S. Pat. No. 5,441,991, 1995). The ion exchange powders, can be produced by either bulk curing of the resin followed by milling (e.g. WO91/09891) to produce a low porosity powder or by reversed phase condensation (Unitaka Ltd U.S. Pat. No. 4,576,969 1986). One of the limitations of these materials was limited internal porosity and they were rapidly replaced by the highly porous sulphonated styrene divinyl benzene copolymer based ion exchange resins when these became available. However, although the phenolic based resins have largely disappeared, specific applications do still exist in food related industries based on their underlying performance characteristics. RU-A-2015996 (Plastmassy) discloses the sulphuric acid catalysed production of ion exchange resins from phenol, formaldehyde and hexamethylene tetramine, but neither discloses nor suggests carbonisation of the resulting resin.

U.S. Pat. No. 6,024,899 (Peng) discloses making mesoporous (>50 vol. % pores in the 2-50 nm size range) carbon by combining a carbon precursor and a pore former which dissolves molecularly into the carbon precursor. The precursor is preferably a phenolic resin owing to its low viscosity, high carbon yield and high degree of cross-linking on curing, a resole resin being preferred. The pore former is preferably a thermoplastic material and has a decomposition or volatilisation temperature above a curing temperature and below a carbonisation temperature of the carbon precursor. The carbon precursor is cured and carbonised., pores being formed by loss of the mass of pore former from the resulting solid solution of pore former in the carbon precursor. In an example a phenolic resole in methanol is mixed with polyvinyl butyral (PVB) also in methanol as pore former so that the amount of PVB is about 15% of that of the phenolic resin. The resulting solution is dip-coated onto a ceramic substrate which is dried, cured at 100° C. and carbonised at 750° C. to give a carbonised product of surface area 200 m²/g and 95% pore volume in the mesopore range. A second example uses polyethylene glycol as pore former and a third example uses coal tar pitch as the pore former. However, the only quoted pore size is for the third example, where the pores are said to be of diameter predominantly 10 nm.

CN-A-1247212 (Shanxi) discloses the production of mesoporous carbon from a phenolic resin using a complex of iron, cobalt or nickel e.g. ferrocene, cobalt acetylacetonate or nickelocene which is effective to give rise to mesopores catalytically after carbonisation when the carbonised resin is activated. Production of mesoporous carbon in bead form is described. In a procedure described in a first example, a novolak (linear phenolic aldehyde resin), hexamethylene tetramine and anhydrous methanol are heated until all the ingredients have dissolved, after which the methanol is vacuum evaporated and the resulting uncured mixture of resin and crosslinker is crushed to give particles of size 450-1250 μm. The particles are alleged to be cured to form beads by dispersion in water containing surfactant and heating to 125° C. after which the beads were heated for a period of about 6 hours to 700° C. to effect carbonisation with a dwell of 30 minutes at 700° C. However, there is no mesoporosity introduced at the resin stage, nor is there mesoporosity introduced at the carbonisation stage. There are no escape paths for gaseous resin decomposition products, so that physical strength, attrition resistance and freedom of dust cannot be expected. Furthermore, steam activation causes the organometallic pore-formers of Shanxi to form mesopores by catalysis of reaction between the carbon and the steam by clusters of metal atoms, but the resulting pores are small (diameters 7.4-9.4 nm, see Table 2 in that specification).

Furthermore, the applicants have repeated the Shanxi experimental work, and although autoclave curing to a hard resinous material was achieved with a strong smell of ammonia/amines that are secondary products of cross-linking reaction of novolak and hexamethylene tetramine, formation of beads could not be obtained either at a relatively low stirrer speed or at the maximum possible stirrer speed. The cured product took the form of several irregular large lumps of hard resin with a colour of ripe peas and some small fibre shaped particles and powder. There was no evidence of mesoporosity on carbonisation and, in contrast to the results reported by Shanxi, only a very low level of mesoporosity on activation.

An alternative route is to carbonise sulphonated styrene—divinylbenzene co-polymers as disclosed in U.S. Pat. No. 4,040,990 and U.S. Pat. No. 4,839,331. These produce carbons directly by pyrolysis with meso/microporosity without recourse to further activation. The materials therefore have good mechanical properties. They are, however, limited to relatively small particle sizes, fixed by the polymer production route, and have a limited range of mesopore structures. They are also very expensive reflecting the high cost of the precursor polymer, the low carbon yields and environmental problems associated with processing polymers containing large amounts of sulphur. The resultant carbons are also contaminated with sulphur, which restricts their use as catalysts supports.

A further route has also been disclosed in U.S. Pat. No. 5,977,016 whereby sulphonated styrene—divinylbenzene co-polymer particles can be formed into pellets in the presence of large volume of concentrated sulphuric acid and then carbonised to give structured materials with both meso- and macroporosity. The route is however complex and expensive with significant environmental problems.

A further route is disclosed in U.S. Pat. No. 4,263,268 where a mesoporous silica with the desired macroshape (i.e. spheres) is impregnated with a carbon forming polymer, such as phenolic or polyfurfuryl resin and then dissolving the silica template in an alkali. This again is a highly expensive route and is only capable of producing the carbon material in a limited range of shapes and forms.

SUMMARY OF THE INVENTION

We have now devised an improved method of producing porous resin structures which can be used to form porous carbons such as mesoporous carbon without, gas phase or chemical activation.

According to the invention there is provided a method for forming a porous resin structure which method comprises the condensation of a nucleophilic component with an electrophilic cross-linking agents in solution in the presence of a pore former.

The condensation can be catalysed or non-catalysed.

The invention also provides a method for forming a porous carbon structure in which the porous resin is carbonised to form the porous carbon structure.

Embodiments of the invention provide a method of making porous carbon, the method comprising:

(a) forming a precursor resin by reacting a nucleophilic component which comprises a phenolic compound or a phenol condensation prepolymer and optionally with one or more modifying reagents selected from hydroquinone, resorcinol, urea, aromatic amines and heteroaromatic amines with an electrophilic cross-linking agent selected from the group consisting of formaldehyde, paraformaldehyde, furfural and hexamethylene tetramine in solution in a pore former selected from the group consisting of a diol, a diol ether, a cyclic ester, a substituted cyclic ester, a substituted linear amide, a substituted cyclic amide, an amino alcohol and a mixture of any of the above with water so that a phase separation occurs between high molecular weight domains and voids of lower molecular weight material and the pore former increases the material in the voids and gives rise to the mesopores in the precursor resin;

(b) removing the pore former from the precursor resin; and

(c) carbonizing the precursor resin in an inert atmosphere at a temperature from 600° C. upwards, micropores developing during said carbonization so that the carbonized material comprises (a) micropores of diameter of up to 20 Å and (b) mesopores of diameter of 2-50 nm from the precursor resin and optionally macropores of diameter >50 nm, said micropores and mesopores being in a bimodal distribution with few pores of size 2-10 nm], the mesopores/macropores providing escape routes for volatile products during carbonisation of the precursor resin.

In further embodiments there is provided porous carbon which is a carbonization and optionally an activation product of a precursor resin;

which has a pore structure that, as estimated by nitrogen adsorption porosimetry, comprises micropores and mesopores/macropores;

said micropores and mesopores/macropores being in a bimodal distribution with few pores of size 2-10 nm; and

the mesopores/macropores providing escape routes for volatile products during carbonisation of the precursor resin.

It will be noted that the above porous carbon is defined to be a carbonization and optionally an activation product of a precursor resin. That feature differentiates the present carbons from porous carbon from natural material and is apparent on microscopic examination. It has a microstructure of micropores and mesopores/macropores in a bimodal distribution with few small mesopores and a large number of pores in the large mesopore/macropore size range which are created by a phase separation in the precursor resin and which survive the carbonisation process. The mesopores/macropores are interconnected and thereby provide escape paths for volatile products during carbonization of the precursor resin. FIG. 14 is an atomic force micrograph of cured resin from novolak, hexamethylene tetramine and ethylene glycol in which dark areas show voids created by pore former in the mesopore/macropore size range. FIG. 15 is an electron micrograph of a bead resulting from carbonisation and activation of a cured resin from novolak, hexamethylene tetramine and ethylene glycol, in which the proportion of ethylene glycol was large so that the pores formed were in the large mesopore/macropore size range, part of the bead being broken away to reveal the internal structure. It will be apparent especially form FIG. 15 that the meso/macropores are open-celled and are interconnected thereby providing paths leading into and from the interior of the bead or other carbonised product. Because gaseous products evolved during carbonization have escape paths, evolution of gaseous products does not damage the structure of the carbonised and optionally activated material The resulting carbonised and activated material has high physical strength and high attrition resistance and is substantially free of carbon dust, especially in bead form, such dust being a major problem associated with other forms of porous carbon in many applications e.g. in the treatment of blood. Furthermore, the interconnected mesopores/macropores in use provide paths into the interior of the material and promote rapid and effective adsorption of desired materials including e.g. relatively large molecules.

Formation of micropores takes place in the carbonisation and activation steps.

As will be apparent from FIGS. 3 a, 3 b and 10 of the present application, there is no significant effect on the mesopores/macropores during carbonisation, and the same is also true during activation

BRIEF DESCRIPTION OF THE DRAWINGS

These and other features, aspects, and advantages of the present invention will become better understood with regard to the following description, appended claims, and accompanying drawings where:

FIG. 1 shows pore former content in the resin composition on the porosity of derived carbonized material with reaction system phenol-formaldehyde-ethylene Glycol-Sulphuric Acid;

FIG. 2 shows the effect of aniline content in resin composition of the reaction system phenol-aniline-formaldehyde-ethylene glycol-sulphuric acid on the porosity of derived carbons;

FIG. 3 a shows the effect of the pore former content on the porosity of phenolic resins with reaction system novolac-hexamine-ethylene glycol;

FIG. 3 b shows the effect the effect of the pore former in resin composition on the porosity of corresponding carbonized materials with reaction system novolac-hexamine-ethylene glycol;

FIG. 4 shows the effect of additions of aniline or urea to the resin compositions of novolac-hexamine-ethylene glycol reaction system on the porosity of resulting carbons;

FIG. 5 shows the effect of the nature of the pore former on the porosity of the carbons derived from the resins of reaction systems novolac-pore former-hexamine;

FIG. 6 shows the effect of the pore former modification with other solvents in the resin compositions based on novolac and hexamine on the porosity of derived carbon;

FIG. 7 shows the effect of carbonization procedure on the porosity of carbons derived from copper-containing resin;

FIG. 8 shows the effect of resin cross-linking conditions on the porosity of derived carbons;

FIG. 9 shows porosity of carbon derived from the resin of novolac-hexamine-furfural-ethylene glycol reaction system;

FIG. 10 shows porosity parameters of the resin prepared in block (novolac-hexamine-ethylene glycol reaction system) and derived carbon;

FIG. 11 shows the effect of different processing of the resin of novolac-hexamine-ethylene glycol-boric acid reaction system on the porosity of derived carbons;

FIG. 12 a shows the effect of ethylene glycol content in block resin composition on the porosity of the resin, reaction system novolac-melamine-formaldehyde-ethylene glycol;

FIG. 12 b shows the effect of the EG content in the composition of the resins prepared in blocks and of the reaction system novolac-melamine-formaldehyde-ethylene glycol on the porosity of derived carbons;

FIG. 13 shows a comparison of porosity of carbons derived from the reaction systems novolac-hexamine-ethylene glycol, novolac-resorcinol-hexamine-ethylene glycol and novolac-hydroquinone-hexamine-ethylene glycol;

FIG. 14 is an atomic force micrograph of cured resin from novolak, hexamethylene tetramine and ethylene glycol in which dark areas show voids created by pore former in the mesopore size range; and

FIG. 15 is an electron micrograph of a bead resulting from carbonisation and activation of a cured resin from novolak, hexamethylene tetramine and ethylene glycol, in which the proportion of ethylene glycol was large so that the pores formed were in the large mesopore/macropore size range, part of the bead being broken away to reveal the internal structure.

DETAILED DESCRIPTION OF PREFERRED EMBODIMENTS

The nucleophilic component can be for example phenol, a phenol formaldehyde pre-polymer—a novolac optionally together with a modifying agent.

The electrophilic component can be for example formaldehyde, hexamine, furfural.

Preferably the pore former acts as the solvent.

Methods for preparation of the porous polycondensation resins generally comprise dissolving nucleophilic components (e.g. phenol, novolac, modifying reagents) and electrophilic cross-linking components (e.g. formaldehyde, hexamine, furfural) in the pore former with or without catalysts (acidic or basic) and thermosetting the solution obtained to produce cured, solid, insoluble and infusible resins with the pore former evenly distributed within the resin matrix creating pores of controlled size.

The invention is particularly useful for producing porous carbons which can be carbonised to mesoporous/macroporous carbons. By mesoporous carbon we mean here a carbon possessing alongside micropores, pores with diameter from ca. 2 nm to ca. 50 nm and by macroporous a carbon possessing alongside micropores pores with diameters larger than 50 nm, as measured by nitrogen adsorption and mercury porosimetry methods and as defined by IUPAC.

Phenol Polycondensation Pre-Polymer

The phenol formaldehyde condensation pre-polymer can be a Novolac resin. Novolac resins are typically produced by the acid catalysed condensation of phenol and formaldehyde in approximately equimolar amounts. Novolacs are usually thermoplastic solid polymers that melt at or above 100° C. depending on the average molecular weight. They are essentially linear chains with molecular weights of from 500 to 2000 D, where phenolic moieties are linked with methylene (predominantly) and methylene ether bridges and possess one nucleophilic active site, predominantly in the unsubstituted ortho-position to hydroxyl group. There can be also varying degrees of chain branching depending upon the production conditions.

Whilst the commercial materials are largely produced using phenol and formaldehyde, a variety of modifying reagents can be used at the pre-polymer formation stage to introduce a range of different oxygen and nitrogen functionality's and cross-linking sites. These include but are not limited to:

1. Hydroquinone and resorcinol. Both are more reactive than phenol and can lead to some cross-linking at the pre-polymer production stage. It is also possible to introduce these compounds at the cross-linking stage to provide different cross-linking paths. These also increase the oxygen functionality of the resins.

2. Nitrogen containing compounds that are active in polycondensation reactions, such as urea, aromatic (aniline) and heteroaromatic (melamine) amines. These allow the introduction of specific types of nitrogen functionality into the initial polymer (and final carbon) and influence the development of the mesoporous structure of both the resins and the final carbons.

Like hydroquinone and resorcinol, all the nitrogen containing nucleophilic modifying reagents which can be used in the present invention possess two and more active sites and are more reactive in condensation reactions than phenol or Novolacs. It means that they are first to react with primary cross-linking agents forming secondary cross-linking agents in situ. In the case of melamine it is preferable to prepare the secondary cross-linking agent—hydroxymethylated melamine—in advance.

Novolacs are thermally stable in that they can be heated and cooled repeatedly without structural change. They are cured on addition of cross-linking agents and heating.

The process of the invention is carried out in solution and the pore former can also be the solvent. For example a solution, obtained from commercial Novolac pre-polymers together with modifying reagents (if required), cross-linking agents and catalysts (if required) and an appropriate amount of the pore former as a solvent, is heated to bring about the cross-linking reaction, resulting in a solid resin.

Alternatively the solid porous polycondensation resins which can be used in the invention can be produced directly from phenol (and optionally modifying agents) and formaldehyde (or other cross-linking agents) on heating their solution in the pore former with the catalyst (acidic or basic).

In both cases the reaction solution will set during the cross-linking reaction if the correct composition is used “locking” the pore former into the resin structure and creating a mesoporous resin.

The-porous resin precursor can be cast into a block and comminuted to give a powder of particle size in the range of 1 to 1000 microns. This resin powder can then be carbonised to give a porous carbon with a pore size which can be controlled e.g. to give a mean pore size of between 2 and 50 nm (mesopores) or greater than 50 nm (macropores) and also with micropores with a mean pore size between 0.6 and 2 nm.

If the viscous solution of the partially cross-linked pre-polymer is poured into a hot liquid such as mineral oil containing a dispersing agent and the mixture stirred, the pre-polymer solution will form into beads. These are initially liquid and then, as curing proceeds, they become solid. The average bead particle size is controlled by several process parameters including the stirrer type and speed, the oil temperature and viscosity, the pre-polymer solution viscosity and volume ratio of the solution to the oil and can be adjusted between 5 and 2000 microns. These beads can then be filtered off from the oil and, after pore former removal, pyrolysed to give meso- or macroporous carbon beads.

It is thought that the mechanism of mesopore generation is due to a phase separation process that occurs during the cross-linking reaction. In the absence of a pore former, as the linear chains of pre-polymer undergo cross-linking, the molecular weight initially increases. Residual low molecular weight components become insoluble in the higher molecular weight regions causing a phase separation into cross-linked high molecular weight domains within the lower molecular weight continuous phase. Further condensation of light components to the outside of the growing domains occurs until the cross-linked phase becomes essentially continuous with residual lighter pre-polymer trapped between the domains.

Pore Formers

There are a large number of solvents that can be employed as the pore formers. The key requirements for these solvents are: high solubility/compatibility of the reaction components in the solvent; useable viscosity of the pre-polymer/cross-linking agent/solvent solution (this for instance essentially rules out glycerol which gives an unacceptably high viscosity); reasonably high boiling temperature to perform the polycondensation reaction at a reasonable rate without significant solvent evaporation.

Pore formers which can be used include but are not limited to: ethylene glycol, 1,4-butylene glycol(diols); diethylene glycol, triethylene glycol(diols-ethers); gamma-butyrolactone, propylene carbonate (cyclic esters); dimethylformamide, N-methyl-2-pyrrolidinone (substituted amides, cyclic and linear); monoethanolamine (aminoalcohol).

In the presence of a low level of pore former the pore former is compatible with, and remains within, the cross-linked resin domains, (e.g., <120 parts/100 parts Novolac for the Novolac-Hexamine-Ethylene Glycol reaction system), whilst the remainder forms a solution with the partially cross-linked polymer between the domains. In the presence of higher levels of pore former, which exceed the capacity of the cross-linked resin, the pore former adds to the light polymer fraction increasing the volume of material in the voids between the domains that gives rise to the mesoporosity. In general, the higher the pore former content, the wider the mesopores and the higher the pore volume.

This phase separation mechanism then provides a variety of ways of controlling the pore development in the cross-linked resin structures. These are: chemical composition and concentration of the pore former; chemical composition and quantity of the cross-linking electrophilic agents, presence, chemical nature and concentration of modifying nucleophilic agents, chemical composition of phenolic nucleophilic components (phenol, Novolac), presence, chemical nature (acidic, basic) and concentration of the catalyst.

To produce the spherical resins by the oil dispersion method referred to above the solvent should also be incompatible with the oil and compatible with water in order to secure the formation of a “water in oil” type emulsion with the beads of the resin solution dispersed in the bulk of the oil, minimise the solvent extraction into the oil and problems with its recovery and enhance simple recovery of the solvent from the solid resin beads by washing with water.

Both protogenic and aprotic solvents of different classes of organic compounds match these requirements and can be used as pore formers, both individually, in mixtures or mixed with water.

Different solvents, though quite similar in structure, will have different compatibilities with the cross-linked resin. This will then alter the phase separation to varying extents and will then affect the porosity of resins and corresponding carbons. Deliberate addition of water to these polar organic solvents will decrease the compatibility of the resin and the resultant pore former, which could be beneficial for some reaction systems, though water, as one of the reaction products, is inevitably present in any reaction where a carbonylic compound is used as the cross-linking agent.

The common feature of amides as the pore formers is that they normally require deliberate addition of water (2-5%) to promote cross-linking with hexamine. When amides are used as the pore formers the final carbons exhibit no mesoporosity detectable by nitrogen adsorption, but they are of relatively low bulk density, which clearly indicates the presence of macropores (>50 nm).

Some pore formers, under special conditions, are also able to contribute to the cross-linking process. For example, active carbocations can be formed from ethylene glycol in strong acidic media or the methylol derivatives of monoethanolamine and formamide with formaldehyde, which will react as secondary cross-linking agents.

Cross-Linking Agents

The primary cross-linking agents used in the invention are formaldehyde, furfural and hexamethylenetetramine (hexamine). Formaldehyde is introduced either in solution in the pore former or as solid paraformaldehyde, (CH₂O)_(x). Formaldehyde cross-links phenolic moieties forming —CH₂— and —CH₂—O—CH₂— bridges at ratios depending on the pH of the reaction mixture. Methylene bridges are the only ones formed in strong acidic and strong alkali media, whereas at pH's close to neutral either type of bridges appear. Water is formed as the stoichiometric secondary condensation product at a level depending on the type of bridge formed. 1 mole per mole of formaldehyde in the case of the methylene bridges or 1 mole H₂O per 2 moles CH₂O in the case of the ether bridges. The “condensation” water may then influence the phase separation and mesopore formation process by reducing the compatibility of the water containing pore former with the resin domain depending on the pore forming solvent being used.

Complete cross-linking of phenol with formaldehyde by methylene bridges requires approximately a 1 to 1.5 molar ratio of the reagents. Taking into account the formation of some ether type bridges, the phenol to formaldehyde molar ratio in the resin compositions of the invention is preferably maintained at 1.6 to 1.8 level. This requires an additional 9 to 12 weight parts of formaldehyde (paraformaldehyde) per 100 weight parts of Novolac resin.

Furfural differs from formaldehyde in that the electrophilic reactivity of its carbonyl group is supplemented by the high nucleophilic activity of the heterocycle. Moreover, ring scission and consecutive reactions can give a wide range of products, which can provide additional cross-linking paths, possibly involving phenolic hydroxyls. These are typical for furan resin derivatives, especially in acidic media and, in combination with other cross linking agents, provide an additional route to modify both the chemical structure and porosity of the resins.

Hexamine can be introduced as a powder directly into the reaction solution. On heating ring cleavage occurs, catalysed by traces of water and, possibly, protonic solvents, resulting in the formation of the active species—aminocarbinols. On cross-linking these form different bridges, including simple methylene and more complex—nitrogen-containing groupings like bis-methylene amine, tris-methylene amine and 1,3-oxazine. The low molecular weight condensation by-products are water, that then cleaves the next portion of hexamine, and ammonia. Ammonia, though highly volatile at the reaction conditions, increases the pH of the reaction solution when no acidic or basic catalysts are present, which may also affect the phase separation and mesopore formation process.

In the present invention hexamine is preferably used for cross-linking Novolac resin at a concentration of 9 weight parts hexamine per 100 weight parts of Novolac. This ensures the formation of the solid resin with maximal cross-linking degree. This is in contrast to previously disclosed sintered resin structures where typically up to 3 parts of hexamine per 100 parts of Novolac were used (EP 0245551). When hexamine is used in the ethylene glycol solution at a level of 3 weight parts per 100 weight parts of Novolac only non-porous semi-solid rubbery material is obtained, whereas at 9 weight parts level a highly mesoporous and solid resin is produced. It is thought that ethylene glycol might act as an internal plasicizer when the cross-linking degree is not adequate.

Modifying Agents

Most of the modifying agents which can be used in the invention contain nitrogen thus introducing this into the resins and therefore the final carbons. Their common feature is their reactivity in condensation reactions, which is higher than that of phenol and Novolac resin. There are at least three distinct ways in which these compounds participate in the condensation process when added in relatively small amounts (5-30 weight % of the phenolic component):

1. Novolac—primary cross-linking agent—modifying agent reaction system. Here the modifying agent reacts rapidly with the primary cross-linking agent forming a secondary cross-linking agent that then binds the Novolac chains together. As a result the resin consists of homocondensed phenolformaldehyde chains bridged with nitrogen-containing groupings (or resorcinol or hydroquinone derived moieties).

2. Phenol—cross-linking agent—modifying agent—strong acidic or strong basic catalyst. Separate homocondensation processes occur for the two different nucleophilic reagents (phenol and modifying agent). This then results in the formation of a binary resin matrixes where the two resin components behave in a different way on thermal treatment.

3. Phenol—cross-linking agent—modifying agent—weak acidic or weak basic catalysts, or no catalyst at all. This leads to a co-condensation process with formation of structurally homogeneous material with modifying moieties evenly distributed within phenolic resin.

For the three different cases the effect of the modifying agent on the porosity of both resin produced and final carbon can be different. Thus, for the reaction system phenol—aniline—formaldehyde—ethylene glycol—sulphuric acid (strong acid as a catalyst) increasing the amount of aniline from 0 to 20 mol. % relative to the phenol leads to a gradual narrowing of mesopores. Conversely in the case of Novolac—aniline—hexamine—ethylene glycol and Novolac—aniline—formaldehyde—ethylene glycol reaction systems (no catalyst at all) increasing the amount of aniline from 0 to 20 weight % relative to the Novolac produces a pronounced increase in both mesopore width and volume.

Reaction Rate Effects

Besides pure catalytic effects, such as increasing the reaction rate and changing the reaction paths, strong acids and alkalis enhance dramatically the solubility and compatibility of growing resin chains and aggregates in the polar pore former due to phenolate formation (for alkalis) or protonation (for acids). Too high catalyst concentrations can also result in enhancing some undesirable reactions, such as decomposition of amide and ester pore formers, disproportionation of aldehydes (alkali catalysed Cannizzaro reaction), blocking of active sites of benzene rings due to sulphonation (with sulphuric acid as a catalyst). Too low catalyst concentrations can result not only in considerable slowing down of condensation reaction, but also in a deterioration of porosity.

The development of mesoporosity within a resin of constant composition is also dependent upon the rate of the cross-linking reaction. The condensation reaction rate can be controlled by the reaction temperature and also via heat transfer phenomena which are controlled by the physical form of the resin (block, beads, etc). This is found in the preparation of the spherical resin, where heat transfer phenomena can be ignored because the process is carried out in hot oil with small resin droplets. If the solid cured spherical resin is prepared from a solution of Novolac and hexamine in ethylene glycol by smoothly increasing the temperature to 100-105° C. (solution quite close to gel state), dispersing the solution into the oil at about the same temperature, and then gradually raising the temperature to 150-160° C. to complete the cross-linking a highly mesoporous resin is formed. Conversely, if the Novolac and hexamine are dissolved in ethylene glycol at 65-70° C. and directly dispersed into the oil at 160-180° C., the mesoporosity of the resulting cured resin will be dramatically decreased. On carbonisation the first resin produces highly mesoporous carbon with moderate to low microporosity. The second resin produces carbon with relatively high microporosity, but low mesoporosity.

It is thought that, when the cross-linking proceeds very quickly under the temperature shock conditions, aggregates of relatively small domains are formed instead of the normal sized domains formed under mild curing conditions. The voids between the small domains in the aggregates then give rise to additional microporosity. And few voids between the aggregates create some mesoporosity.

It has also been found that the way in which the pore former is removed from the cured resin can be important to the generation of the porosity in corresponding carbon. If the pore former (e.g., ethylene glycol) is removed simply on pyrolysis during the carbon production, the mesoporosity may be lost. It has been found that it is preferable to remove the pore former at a low temperature, e.g., below 100° C., via washing the resin with water or vacuum distillation, with subsequent recycling of the pore former. The washing (sometimes—after neutralisation) becomes absolutely necessary, when alkalis or sulphuric acid are used as catalysts. This is because alkalis will affect the carbonisation process, sometimes in very undesirable way, whereas sulphuric acid will contaminate the carbon with sulphur, reducing its value as a catalysts supports.

Other Additions

It has also been found that hetero atoms can be incorporated in the resin structure. Metals such as copper, nickel, chromium etc, can be incorporated in the porous resin structure by incorporating the metal as a solution of a salt in the pore forming solvent prior to cross linking the resin and non-metals and metalloids can be incorporated directly into the mesoporous resin and thence into the mesoporous carbons. Where an inorganic compound is soluble in the pore former it can be added directly to the initial reaction solution. The preparation procedure is then carried out in the usual way. The metal species are then evenly distributed within the resin matrix. In some cases the ability of the element to complex with or have some other specific interaction with, the hydroxyl or amino groups of phenolic resin enhances the initial distribution to the atomic level. Incorporation of the highly dispersed element within the resin then leads to a high dispersion of the element in the carbon formed during pyrolysis.

Carbonisation and Activation

The transformation of the porous resins in any physical form and shape into the porous carbons of the invention is performed by carbonisation, i.e. high temperature treatment in an inert atmosphere and at temperatures from ˜600° C. upwards. The pyrolysis process commences at about 400° C. and is largely complete by around 700° C. although further small weight losses continue up to around 1400° C. However surface area development is only significant above around 600° C. at which point the material is not strictly carbon. The development of a significant electrical conductivity is only observed at above 700° C. The inert atmosphere for the pyrolysis can be secured by the appropriate gas flow. Nitrogen and argon can be used as inert purge gases at any temperature whilst carbon dioxide is effectively inert up to around 800° C. in the absence of catalytic metals. Vacuum may also be used although this can lead to the development of molecular sieving behaviour. Due to the presence of mesopores in these materials, which provide efficient escape routes for the volatile products, the heating rates employed can be very high—up to 10° C. per minute. The porosity of the carbons can be further enhanced by conventional activation methods, e.g. by activation in steam above 750° C. or carbon dioxide above 800° C., which can give surface areas as measured by BET 5 point method of up to 2000 m²/g. It has been found that “physical” activation with carbon dioxide at the temperatures in the range 850-900° C. gives rise predominantly to microporosity, whereas air activation at 420-450° C. enhances rather mesopore size and volume e.g. in the same pore size and range as in the original carbon.

It is a feature of the present invention that it enables there to be produced spherical porous carbon structures with a controlled range of particle size e.g. where the size distribution of the spheres can be controlled to give a dispersion of D90/D10 of better than 10 (preferably better than 5) and the larger pores can be controlled from a mean diameter of 2 nm up to 50 nm (mesopores) or greater than 50 nm (macropores) and where the mean micropore diameter can be controlled to between 0.6 and 2 nm to give BET surface areas from 250 to 800 m²/g without recourse to conventional activation procedures.

The materials of the present invention can be advantageously used in a wide variety of demanding applications where the high physical strength and high attrition resistance offer special benefits. These include, but are not limited to, liquid phase catalyst supports, blood filtration and any application where the carbon is used in a fluid bed or moving bed environment. The large mesopores can also be advantageously utilised in system where larger molecules are either adsorbed or grafted within the pores. These can include drug release systems, chiral supports etc.

The invention is illustrated in the following examples.

EXAMPLE 1

A reaction mixture containing 94 weight parts of phenol, 54 weight parts of paraformaldehyde (PF) (phenol to formaldehyde molar ratio 1:1.8), specified amounts of ethylene glycol (EG) pore former and concentrated sulphuric acid (SA) was heated with stirring up to specified condensation temperature (paraformaldehyde dissolves completely at about 60° C.) and maintained at this temperature for a specified residence time (Table 1-1).

TABLE 1-1 EG, SA, Condensation Residence # weight parts weight parts temperature, ° C. time, minutes 1 259 35.4 72 ± 1 80 2 370 45 77 ± 1 120 3 259 17.0 72 ± 1 300

The resulting viscous solution was poured as a stream into 2-4 volumes of stirred preheated (110-115° C.) mineral oil containing 0.5% of a drying oil, acting as a dispersing agent. The temperature of the resulting mixture dropped to ˜100-102° C., and cross-linking occurred normally within 1-2 minutes. The resulting slurry was gradually heated up to 115-120° within 30-60 minutes to complete the curing and cooled down. Resin in bead form was filtered off from the oil, washed several times with hot water to remove both pore former and catalyst. The resulting porous spherical resin, containing water, residual oil, traces of pore former and catalyst can then be directly carbonised to produce spherical porous carbon

For analysis of the resin it can be washed repeatedly with organic solvent, preferably with ethanol-ether 1:1 v/v solution, and dried in vacuo until constant weight. The pore size distribution graphs and some structural parameters of carbonised materials, formed by heating at 800° C., in carbon dioxide flow, are given in FIG. 1 and Table 1-2. In which the effect of the pore former content and catalyst's concentration in the resin composition on the porosity of derived carbonised material is shown. Reaction system Phenol—Formaldehyde—Ethylene Glycol—Sulphuric Acid.

TABLE 1-2 BET area, Pore Volume Bulk Density, m²/g (P/P₀ = 0.98), cm³/g g/cm³ Carbon 1.1 571.1 0.58 0.34 Carbon 1.2 598.2 0.90 0.32 Carbon 1.3 475.7 0.26 0.69

EXAMPLE 2

A reaction mixture containing 94 weight parts of phenol, specified amounts of aniline (A), ethylene glycol pore former, paraformaldehyde and concentrated sulphuric acid was heated with stirring up to specified condensation temperature (complete paraformaldehyde dissolution occurs around 60° C.) and maintained at this temperature for specified residence time (see Table 2-1).

TABLE 2-1 EG, PF, A, SA, weight weight weight weight Condensation Residence # parts parts parts parts temp. ° C. time, min. 1 272 56.7 4.7 37.2 73 ± 1 105 2 284 59 9.3 39 73 ± 1 115 3 310.5 64.8 18.6 42.4 73 ± 1 140 4 336.2 70.2 27.9 45.9 73 ± 1 180

The resulting viscous solution was poured in a stream into 2-4 volumes of stirred preheated (110-115° C.) mineral oil containing 0.5% of the drying oil and the resin was processed further in the same way as in Example 1. The pore size distribution graphs and some structural parameters of carbons 2.1 to 2.4 and carbon 1.1 are compared in FIG. 2 and Table 2-2, in which is shown the effect of aniline content in resin composition of the reaction system Phenol—Aniline—Formaldehyde—Ethylene glycol—Sulphuric acid on the porosity of derived carbons.

TABLE 2-2 BET area, Pore Volume Bulk Density, m²/g (P/P₀ = 0.98), cm³/g g/cm Carbon 1.1 571.1 0.58 0.34 Carbon 2.1 526.7 0.78 0.40 Carbon 2.2 516.7 0.31 0.76 Carbon 2.3 441.8 0.24 0.87 Carbon 2.4 293.9 0.16 0.83

EXAMPLE 3

Industrial Novolac resin in amount of 100 weight parts was mixed together with specified amount of ethylene glycol pore former (see Table 3-1) at elevated temperature and with stirring to enhance the formation of a clear solution, which was then cooled down to 65-70° C., where hexamine (HA) in amount of 9 weight parts was added. The resulting stirred mixture was gradually heated at such a rate as to reach the specified temperature in specified residence time (see Table 3-1).

TABLE 3-1 Ultimate pre- Condensation EG, weight EG: condensation residence time, # parts Novolac + HA temp., ° C. min. 1 109 1.00 85 30-35 2 136.3 1.25 90 30-35 3 163.5 1.50 100 45-50 4 190.8 1.75 102 70-75 5 218 2.00 104 75-80 6 272.5 2.50 105 75-80 7 327 3.00 105 80-85 8 381.5 3.50 106 80-85 9 436 4.00 107 85-90

The viscous solution was then poured in stream into 2-4 volumes of stirred preheated (115-120° C.) mineral oil containing 0.5% of the drying oil. The temperature of resulting emulsion dropped to 105-110° C., but on further heating cross-linking occurred at about 115-120° C. Further heating at the rate about 0.5° C. per minute up to 150° C. was applied to complete the curing. After cooling down the resin beads were filtered off from the oil and washed several times with hot water to remove the pore former and small amount (less than 5% of total) of low molecular weight polymer. The resulting porous spherical resin, containing water, residual oil, traces of pore former and low molecular weight fraction was carbonised by heating at 800° C. in flowing carbon dioxide to produce the spherical porous carbon. If the resin beads are carbonised directly after separation from the oil, without washing, the porosity of resulting carbons decreases. For analysis the sample of resin should be washed repeatedly with organic solvent, preferably with ethanol-ether 1:1 v/v solution, and dried in vacuo until constant weight. The pore size distribution graphs and some structural parameters of both resins and carbonised materials are presented on FIGS. 3 a and 3 b and Tables 3-2 and 3-3, respectively.

TABLE 3-2 BET area, Pore Volume m²/g (P/P₀ = 0.98), cm³/g Resin 3.1 Non-porous Non-porous Resin 3.2 Slightly porous Slightly porous Resin 3.3  98.9 0.35 Resin 3.4 118.2 0.54 Resin 3.5 141.1 0.81 Resin 3.6 144.7 0.97 Resin 3.7 111.3 0.67 Resin 3.8 134.9 0.76 Resin 3.9 120.0 0.66

FIG. 3 b shows the effect of the pore former in resin composition on the porosity of corresponding carbonised materials. Reaction system Novolac—Hexamine—Ethylene Glycol for carbons 3.1 to 3.9.

TABLE 3-3 BET area, Pore Volume m²/g (P/P₀ = 0.98), cm³/g Carbon 3.1 473.2 0.26 Carbon 3.2 468.3 0.30 Carbon 3.3 592.2 0.48 Carbon 3.4 567.3 0.54 Carbon 3.5 579.6 0.88 Carbon 3.6 525.1 1.02 Carbon 3.7 469.3 1.13 Carbon 3.8 482.0 0.84 Carbon 3.9 524.8 1.06

EXAMPLE 4

Industrial Novolac resin (N) in amount of 100 weight parts was mixed together with specified amount of ethylene glycol pore former (EG) (see Table 4-1) at elevated temperature and on stirring to enhance the formation of clear solution, which then was cooled down to 65-70° C. where specified amounts of hexamine (HA) and modifying agent (MA)—aniline (A) or urea (U), were added.

TABLE 4-1 EG, HA, EG: RT, # w.p. w.p. A, w.p. U, w.p. N + HA + MA CT, ° C. min 1 246.4 13.2 10 — 2.0 91 35 2 288 24 20 — 2.0 80 50 3 246.4 13.2 — 10 2.0 103 75 4 288 24 — 20 2.0 103 60

The resulting stirred mixture was gradually heated at such a rate as to reach the specified temperature (CT) in specified residence time (RT) (Table 4-1). Then the viscous solution was poured as a stream into 2-4 volumes of stirred pre-heated (110-115° C.) mineral oil containing 0.5% of the drying oil. The temperature of the resulting emulsion dropped to 100-105° C., but on further heating cross-linking occurred at about 105-110° C. Further heating at a rate of about 0.5° C. per minute up to 150° C. was applied to complete the curing. After cooling down the resin beads were processed further in the same way as in Example 3. The pore size distribution graphs and some structural parameters of the carbonised materials carbons 4.1 to 4.4 (800° C., flowing carbon dioxide) are compared with those of the carbon 3.5 in FIG. 4 and Table 4-2

TABLE 4-2 BET area, Pore Volume m²/g (P/P₀ = 0.98), cm³/g Carbon 3.5 578.6 0.88 Carbon 4.1 612.6 0.77 Carbon 4.2 629.6 0.81 Carbon 4.3 648.1 0.73 Carbon 4.4 717.0 1.08

EXAMPLE 5

A clear solution of 100 weight parts of industrial Novolac resin in 327 weight parts of specified pore former (see Table 5-1) was heated up to 65-70° C. where 9 weight parts of hexamine were added. The resulting reaction mixture was gradually heated on stirring to reach the ultimate condensation temperature of 105-107° C. in 75-80 minutes.

TABLE 5-1 # Pore Former, weight parts PCT, ° C. RT, min 1 1,4-Butylene glycol, 327 105 85 2 1,2-Propylene carbonate, 327 108 70 3 Di(ethylene glycol), 327 103 90 4 Tri(ethylene glycol), 327 104 80 5 γ-Butyrolactone, 191 - Water, 11 106 60 6 Dimethylformamide, 278 - Water, 5.5 120 100 7 N-Methyl-2-pyrrolidinone, 327 -Water, 5.5 122 80

Then the viscous solution was poured as a stream into 2-4 volumes of stirred pre-heated (115-120° C.) mineral oil containing 0.5% of the drying oil. The temperature of the resulting emulsion dropped to 110-115° C., but on further heating cross-linking occurred, normally at about 120° C. The further processing was the same as in Examples 3 and 4. The pore size distribution graphs and some structural parameters of carbonised materials obtained by heating at 800° C., in carbon dioxide or nitrogen flow, carbons 5.1 to 5.8 are presented in FIG. 5 and Table 5-2 and compared with those of carbon 3.7.

TABLE 5-2 BET area, Pore Volume Bulk Density, m²/g (P/P₀ = 0.98) cm³/g g/cm³ Carbon 3.7 469.3 1.13 0.30 Carbon 5.1 586.0 0.57 0.47 Carbon 5.2 621.0 0.92 0.67 Carbon 5.3 556.4 0.37 0.76 Carbon 5.4 548.1 0.33 0.75 Carbon 5.5 498.5 0.27 0.73 Carbon 5.6 524.2 0.28 0.33 Carbon 5.7 511.8 0.28 0.33

EXAMPLE 6

A clear solution of 100 weight parts of industrial Novolac resin and 9 weight parts of hexamine in 327 weight parts of the pore former of specified composition (see Table 6-1) was processed exactly as in Example 5.

TABLE 6-1 # Di(ethylene glycol), w.p. Ethylene glycol, w.p. Water, w.p. 1 272.5 — 54.5 2 218 — 109 3 163.5 163.5 —

The pore size distribution graphs and some structural parameters of carbonised materials obtained by heating at 800° C., in flowing carbon dioxide are presented in FIG. 6 and Table 6-2 carbons 6.1 to 6.3 and compared with those of carbon 5.3.

TABLE 6-2 BET area, Pore Volume m²/g (P/P₀ = 0.98) cm³/g Carbon 5.3 556.4 0.37 Carbon 6.1 561.2 0.39 Carbon 6.2 585.0 0.38 Carbon 6.3 606.1 0.58

EXAMPLE 7

A reaction solution containing 100 weight parts of industrial Novolac resin, 12 weight parts of hexamine, 7 weight parts of anhydrous copper(II) sulphate, 190.4 weight parts of ethylene glycol and 33.6 weight parts of monoethanolamine (catalyst and pore former) was gradually heated from 60 to 100° C. in 35-40 minutes. Then the viscous solution was poured in a stream into stirred pre-heated (115-120° C.) mineral oil containing 0.5% of the drying oil. After the initial drop in the resulting emulsion temperature to 110-112° C. further heating was applied at the rate 0.5° C. per minute up to 150° C. Normally cross-linking occurred at 115-120° C. The processing of the resin in beads was the same as in Examples 3-6. FIG. 7 and Table 7 present pore size distributions and some structural parameters of the carbons derived from this resin and containing ca. 5% weight. of finely dispersed copper. Carbon 7.1 was prepared by heat treatment of the resin at 800° C. in flowing carbon dioxide. Carbon 7.2 was prepared by heat treatment of the resin at 800° C. in flowing nitrogen.

TABLE 7 BET area, Pore Volume m²/g (P/P₀ = 0.98), cm³/g Carbon 7.1 479.3 0.55 Carbon 7.2 444.5 0.59

EXAMPLE 8

Industrial Novolac resin in amount of 100 weight parts was mixed together with 327 g of ethylene glycol at elevated temperature and on stirring to enhance the formation of clear solution, which then was cooled down to 65° C. where hexamine in amount of 9 weight parts was added. Resulting stirred mixture was briefly heated up to 70° C. just to ensure dissolution of hexamine and poured in stream into 3 volumes of stirred preheated (190° C.) mineral oil containing 0.5% of the drying oil. The temperature of resulting emulsion dropped to 160° C., and almost immediately (less than in 1 min) cross-linking occurred. The temperature of the reaction mixture was raised up to 175° C. in 15 min to complete the curing. After cooling down the resin in beads was filtered off from the oil and further processed in a way similar to Example 3. The pore size distribution graph and some structural parameters of the carbon produced from the resulting resin, cross-linked under severe conditions, (Carbon 8, 800° C., carbon dioxide) are compared on FIG. 8 with corresponding properties of the carbon (Carbon 3-7) derived from the compositionally similar resin, but cross-linked under mild conditions (Example 3, 7).

EXAMPLE 9

Industrial Novolac resin in amount of 100 weight parts was mixed together with 236 weight parts of ethylene glycol at elevated temperature and on stirring to enhance the formation of clear solution, which then was cooled down to 65° C., where hexamine in amount of 3 weight parts and furfural in amount of 15 weight parts were added. Resulting stirred mixture was gradually heated to reach 110° C. in 1 hr, and viscous solution was poured in stream into 3 volumes of stirred preheated (120° C.) oil, containing 0.5% of the drying oil. On further heating curing occurred at 140-145° C. (in 15-20 min.). After further heating to complete curing (up to 155° C. in 20 min.) and cooling resin in beads was filtered off and processed as described in Examples 3-6. Porosity parameters of corresponding carbon are presented in FIG. 9.

EXAMPLE 10

Industrial Novolac resin in amount of 100 weight parts was mixed together with 218 weight parts of ethylene glycol at elevated temperature and on stirring to enhance the formation of clear solution, which then was cooled down to 65-70° C., where hexamine (HA) in amount of 9 weight parts was added. Resulting stirred mixture was gradually heated at such a rate as to reach 95-97° C. in 70 min. Then the hot viscous solution was poured into shallow trays either made of or lined with inert material (e.g., Pyrex™ glass or metal lined with PTFE film) that were consequently sealed to minimise the pore former loss. Trays were put into suitable preheated (100° C.) oven. The temperature within the oven was gradually raised to reach 150° C. in an hour and maintained at this level for another hour. After cooling resulting solid blocks of resin were crashed to give particles with maximal size of 1 cm. Crushed resin was washed several times with hot water and dried at 80-100° C. on air. Dry resin could be milled, classified and carbonised in a normal way to produce mesoporous carbon of desired particle size but irregular shape of particles. If the resin is carbonised directly after crashing without washing, the mesoporosity of resulting carbon decreases essentially. The pore size distribution graphs and some structural parameters of both resin and carbonised material (800° C., carbon dioxide flow) are presented in FIG. 10. Similar procedures could be applied for the preparation in blocks of all the other resins of the invention.

EXAMPLE 11

Reaction solution consisting of 100 weight parts of industrial Novolac resin, 9 weight parts of hexamine, 20 weight parts of boric acid and 258 weight parts of ethylene glycol was heated up from 70 to 100° C. in 45 min. Resulting viscous solution was poured in stream into 3 volumes of stirred preheated (105° C.) oil, containing 0.5% of the drying oil. On further heating curing occurred at around 110° C. Further heating was applied up to 160° C. in 30 min. to complete the curing. After filtering the resin beads off further treatment prior to carbonisation was applied in three different ways:

1—No treatment at all.

2—Several washings with hot water.

3—Extraction with ether in Soxhlett apparatus.

Pore size distribution graphs of the resulting carbons 11.1 to 11.3 and other parameters are compared in FIG. 11 and Table 11.

TABLE 11 B₂O₃ Bulk BET area, Pore volume content, Density, m²/g (P/P_(o) = 0.98), cm³/g % g/cm³ Carbon 11.1 303.1 0.41 6.8 0.47 Carbon 11.2 410.0 0.79 5.3 0.36 Carbon 11.3 346.3 0.57 6.6 0.38

EXAMPLE 12

A solution containing 100 weight parts of industrial Novolac resin (N), 194.4 weight parts of clear solution made of 27.54 weight parts of Melamine (M), 26.18 weight parts of Paraformaldehyde (PF) and 140.68 weight parts of Ethylene Glycol (EG), and additionally—specified amount of Ethylene Glycol (EG) (Table 12-1) was placed into glass tray, sealed, put into preheated oven and kept at 140±5° C. for 15 hours, though gelation occurs within first 2-3 hours. After cooling down the resin in block was further processed as in Example 10. The pore size distribution graphs and some structural parameters of both resins and carbonised materials (800° C., carbon dioxide flow) are presented in FIG. 12 a, 12 b and Table 12-2.

TABLE 12-1 Additional EG, Σ EG/ Gelation # weight parts (N + M + PF) time, hrs 1 89.85 1.5 2.00 2 243.55 2.5 2.50 3 320.40 3.0 2.75 4 474.10 4.0 3.00

TABLE 12-2 BET area, Pore Volume m²/g (P/Po = 0.98), cm³/g Resin 12.1 Non-porous Non-porous Resin 12.2 193.9 0.41 Resin 12.3 202.4 0.38 Resin 12.4 120.9 0.24 Carbon 12.1 436.2 0.24 Carbon 12.2 608.8 0.53 Carbon 12.3 612.8 0.77 Carbon 12.4 577.4 0.49

EXAMPLE 13

Industrial Novolac resin (N) in amount of 100 weight parts was dissolved in specified amount of Ethylene Glycol (EG). The solution of 10 weight parts of Resorcinol (R) or Hydroquinone (Hq) in 30 weight parts of EG was added to the Novolac solution together with 12 weight parts of Hexamine (HA). Resulting reaction solution was heated up to a specified temperature for a specified time (Table 13-1), poured into a stirred hot oil (120° C.) containing 0.5% of the drying oil and processed further as described in Examples 3-6. Properties of the carbons derived from the resins thus obtained are compared with the properties of carbons 3.2 and 3.4 in FIG. 13 and Table 13-2.

TABLE 13-1   # EG, weight parts R, weight parts Hq, weight parts $\frac{\sum{EG}}{N + {HA} + {R({Hq})}}$ $\frac{{{Ultimate}\mspace{14mu} {solution}\mspace{14mu} {{temp}.}},{{\circ \; C}.}}{{{Residence}\mspace{14mu} {time}},{\min.}}$ 1 122.5 10 — 1.25  90/40 2 183.5 — 10 1.75 103/60

TABLE 13-2 BET area, Pore Volume m²/g (P/Po = 0.98), cm³/g Carbon 3.2 468.3 0.30 Carbon 3.4 567.3 0.54 Carbon 13.1 754.9 0.57 Carbon 13.2 676.1 0.94 

1. Porous carbon: which is a carbonization and optionally an activation product of a precursor resin; which has a pore structure that, as estimated by nitrogen adsorption porosimetry, comprises micropores and mesopores/macropores; said micropores and mesopores/macropores being in a bimodal distribution with few pores of size 2-10 nm; and the mesopores/macropores providing escape routes for volatile products during carbonisation of the precursor resin.
 2. The carbon of claim 1, wherein the micropores are the result of carbonization of the precursor resin and optionally activation of the resulting carbonized material and the mesopores/macropores are the result of phase separation during cross-linking of the precursor resin in a pore-forming solvent.
 3. The carbon of claim 1, wherein the value for the differential of pore volume V with respect to the logarithm of pore radius R (dV/dlogR) for the mesopores/macropores is greater than 0.2 for at least some values of pore size in the range >20 nm.
 4. The carbon of claim 1, in which catalytic metal is absent.
 5. The carbon of claim 1, in which contaminant sulphur is absent.
 6. The carbon of claim 1, which is unactivated and has a BET surface area of 250 to 800 m²/g.
 7. The carbon of claim 1, which is activated and has a BET surface area of 800 to 2000 m²/g.
 8. The carbon of claim 1, which is in the form of a powder.
 9. The carbon of claim 1, which is in the form of beads.
 10. A method of making porous carbon, the method comprising: (a) forming a precursor resin by reacting a nucleophilic component which comprises a phenolic compound or a phenol condensation prepolymer optionally with one or more modifying reagents selected from hydroquinone, resorcinol, urea, aromatic amines and heteroaromatic amines with an electrophilic cross-linking agent selected from the group consisting of formaldehyde, paraformaldehyde, furfural and hexamethylene tetramine in solution in a pore former selected from the group consisting of a diol, a diol ether, a cyclic ester, a substituted cyclic ester, a substituted linear amide, a substituted cyclic amide, an amino alcohol and a mixture of any of the above with water so that a phase separation occurs between high molecular weight domains and voids of lower molecular weight material and the pore former increases the material in the voids and gives rise to the mesopores in the precursor resin; (b) removing the pore former from the precursor resin; and (c) carbonizing the precursor resin in an inert atmosphere at a temperature from 600° C. upwards, micropores developing during said carbonization so that the carbonized material comprises (a) micropores of diameter of up to 2 nm and (b) mesopores of diameter of 2-50 nm and optionally macropores of diameter >50 nm from the precursor resin, said micropores and mesopores/micropores being in a bimodal distribution with few pores of size 2-10 nm, the mesopores/macropores providing escape routes for volatile products during carbonisation of the precursor resin.
 11. The method of claim 10, which comprises forming the precursor resin by reacting a novolak with hexamethylene tetramine in solution in ethylene glycol as pore former.
 12. The method of claim 10, wherein precursor resin is formed under conditions such that the solution sets during the reaction so that the pore former becomes locked into the resin structure as the mesoporous precursor resin is created.
 13. The method of claim 12, further comprising casting the resin precursor into a block and comminuting the block to form a powder.
 14. The method of claim 10, further comprising dispersing the solution in a mineral oil heating the oil to form beads of the precursor resin.
 15. The method of claim 10, further comprising activating the resin. 